EP2773785B1 - Duplexedelstahl - Google Patents

Duplexedelstahl Download PDF

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EP2773785B1
EP2773785B1 EP12846399.9A EP12846399A EP2773785B1 EP 2773785 B1 EP2773785 B1 EP 2773785B1 EP 12846399 A EP12846399 A EP 12846399A EP 2773785 B1 EP2773785 B1 EP 2773785B1
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stainless steel
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austenitic stainless
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EP2773785A1 (de
EP2773785A4 (de
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Alexander Thulin
Jan Y. JONSSON
Rachel PETTERSSON
Jan-Olof Andersson
Staffan Hertzman
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Outokumpu Oyj
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Outokumpu Oyj
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite

Definitions

  • This invention relates to a duplex ferritic austenitic stainless steel, which chemical composition and microstructure are favorable for use in chemical industries wherein good uniform corrosion resistance and high strength are required.
  • One target of use for the steel is in urea manufacturing.
  • intermetallic precipitates such as sigma phase
  • the sigma phase forms in a temperature range of 600 - 1000 °C and has particular importance, because already a small amount, even less than 1 volume %, of the sigma phase causes a considerable reduction in plasticity, in impact toughness and impairment in corrosion resistance.
  • the fastest kinetics of sigma phase formation occurs at 800-900 °C.
  • the sigma phase can only be dissolved by annealing above 1050 °C. In the presence of large quantities of chromium and molybdenum, the tendency for sigma phase precipitation increases.
  • the US patent 5,582,656 relates to a duplex ferritic austenitic stainless steel which contains max 0,05 weight % C, max 0,8 weight % Si, 0,3-4 weight % Mn, 28-35 weight % Cr, 3-10 weight % Ni, 1,0-4,0 weight % Mo, 0,2-0,6 weight % N, max 1,0 weight % Cu, max 2,0 weight % W, max 0,01 weight % S and 0-0,2 weight % Ce, balance being iron.
  • Mo, W, Si and Mn chromium increases the risk of precipitation of intermetallic phases.
  • copper improves the general corrosion resistance in acid environments, such as sulphuric acid, but high contents of copper decrease the pitting and crevice corrosion resistance.
  • the ferrite content in the microstructure is 30-70 volume %, the balance being austenite.
  • the steel is very suitable in the environments that exist in urea production.
  • the US patent 7,347,903 describes a duplex stainless steel for urea manufacturing plants.
  • the steel contains less than 0,03 weight % C, less than 0,5 weight % S, less than 2 weight % Mn, 26-28 weight % Cr, 6-10 weight % Ni, 0,2-1,7 weight % Mo, 2-3 weight % W, 0,3-0,4 weight % N, with the balance being iron and impurities, in which the copper content as an impurity is not more than 0,3 weight %.
  • a greater content of copper accelerates corrosion in the corrosive environment of a urea manufacturing.
  • the sensitivity to sigma phase precipitation during welding is extremely low compared with general duplex stainless steels.
  • the tensile strength is high which allows the use in urea plants.
  • the US patent 3,567,434 relates to stainless steels which contain in weight % 0,01-0,1 C, 0,2-2,0 Si, 0,2-4,0 Mn, 23-30 Cr, 4-7 Ni, 1-5 Mo, 1-4 Cu, 0,06-0,4 N, the rest being Fe and inevitable impurities in such conditions that the ratio Cr/Ni in weight % shall be at the range of 3,8-6,25 and the ratio (Ni+200xN)/Cr in weight % shall be at the range of 0,74-3,72.
  • the corrosion resistance especially in sulphuric acid environments, is improved by the addition of molybdenum and copper.
  • Other properties, such as ductility, elongation, are improved and cracking during welding is eliminated by the addition of nitrogen.
  • the US patent 4,612,069 describes a pitting resistant duplex stainless steel which contains in weight % ⁇ 0,08 C, ⁇ 2,0 Si, ⁇ 2,0 Mn, 23-29 Cr, 5-9 Ni, ⁇ 1,0 Mo, 0,5-3,5 Cu, ⁇ 0,2 N, the rest being Fe and inevitable impurities.
  • the copper addition improves the pitting resistance of the austenite, particularly in acidic chloride-thiosulfate solutions.
  • the stainless steel of this US patent can be furnace cooled from a high temperature to have low levels of residual stress and the sigma and other embrittlement phases are minimized during this slow furnace cooling.
  • Intermetallic phases are also problems for the stainless steels which are applied in chloride environments, such as sea water.
  • the EP publication 545753 relates to a duplex stainless steel to be used in chloride-containing environments.
  • the steel has a chemical composition consisting essentially, on a weight %, of: C: 0.03% or less, Si: 1.0% or less, Mn: 1.5% or less, P: 0.040% or less, S: 0.008% or less, sol.Al: 0.040% or less, Ni: 5.0 - 9.0%, Cr: 23.0 - 27.0%, Mo: 2.0 - 4.0%, N: 0.24 - 0.32%, W: greater than 1.5% and at most 5.0%, optionally at least one element selected from the group consisting of Cu: 0.2 - 2.0% and V: 0.05 - 1.5% and/or the group consisting of Ca: 0.02% or less, Mg: 0.02% or less, B: 0.02% or less, and one or more rate earth metals: 0.2% or less in total.
  • the pitting resistance equivalent PREW with the formula PREW %Cr+3.3(%Mo+0.5%W)+16%N has a value of at least 40 using the element contents being in weight %.
  • the EP publication 2050832 provides a duplex stainless steel to be used chloride environment as a material in seawater desalination plants, facilities and equipment.
  • the steel contains, weight %, C: 0.06% or less, Si: 0.05 to 3.0%, Mn: 0.1 to 6.0%, P: 0.05% or less, S: 0.010% or less, Ni: 1.0 to 10.0%, Cr: 18 to 30%, Mo: 5.0% or less, Cu: 3.0% or less, N: 0.10 to 0.40%, Al: 0.001 to 0.08% or less, Ti: 0.003 to 0.05%, Mg: 0.0001 to 0.0030%, and O: 0.010% or less, having a product of an activity coefficient f N of N, Ti content, and N content f N TiN of 0.00004% 2 or more, and having a product of Ti content and N content TixN of 0.008% 2 or less.
  • the WO publication 96/39543 describes a duplex stainless steel applied to marine facility.
  • the steel is composed of in weight %: less than 0.03 % of C, less than 1.0 % of Si, less than 2.0 % of Mn, less than 0.04 % of P, less than 0.004 % of S, less than 2.0 % of Cu, 5.0 - 8.0 % of Ni, 22 - 27 % of Cr, 1.0 - 2.0 % of Mo, 2.0 - 5.0 % of W, and 0.13 - 0.30 % of N.
  • one or two elements selected from a group consisting of: less than 0.03 % of Ca, less than 0.1 % of Ce, less than 0.005 % of B and 0.5 % of Ti.
  • the WO publication 03/080886 describes a high-grade duplex stainless steel with suppressed formation of intermediate phases, such as sigma and vic phases.
  • the amount of intermetallic phases are reduced by delaying diffusion and precipitation of intermetallic phases adding appropriate amounts of Ba, Y, Ce, La, Nd, Pr, Ta, Zr, and Ti as well as additionally blocking of Cr, Mo, Si and W using minute REM compounds or Ba oxides with much larger atomic diameter.
  • the chemical composition consists essentially, on a weight basis, of Cr 21.0% - 38.0%, Ni 3.0% - 12.0%, Mo 1.5% -.6.5%, W 6.5% or less, Si 3.0% or less, Mn 8.0% or less, N 0.2% - 0.7%, C 0.1% or less, at least one element selected from the group consisting of Ba 0.0001 - 0.6% and one or more elements of Mischmetal (MM) and Y 0.0001 - 1.0% in total..
  • the object of the present invention is to eliminate some drawbacks of the prior art and to achieve a new duplex ferritic austenitic stainless steel which chemical composition is optimized with the focus on the production and the manufacturing of the duplex stainless steel itself.
  • the introduction of a formula to predict the sensitivity to sigma phase formation significantly helps to select the alloys best suited for industrial production, while the corrosion properties are maintained to be favorable for chemical industry applications, where good uniform corrosion resistance and high strength are required.
  • the microstructure of the duplex ferritic austenitic stainless steel consists of 35-65 volume % of ferrite, with a preferred content in the range 45-55 volume % of ferrite, the balance being austenite.
  • the chemical composition of the invention consists of less than 0,03 weight % carbon, less than 1 weight % silicon, 3 weight % or less manganese, 26-29,5 weight % chromium, 5-8,5 weight % nickel, 1-3 weight % molybdenum, 0,25-0,35 weight % nitrogen, 1-3 weight % copper and the rest of the chemical composition being iron and inevitable impurities occurring in stainless steels.
  • Sulphur should be limited to less than 0,010 weight % and preferably less than 0,005 weight %.
  • the phosphorus content should be less than 0,040 weight % and the sum of sulphur and phosphorus (S+P) less than 0,04 weight %.
  • the aluminium content should be maximized to less than 0,04 weight % and preferably maximum less than 0,03 weight %, and the total oxygen level below 100 ppm and preferably below 50 ppm.
  • up to 1 weight % tungsten and up to 1 weight % of cobalt can be added in the duplex stainless steel of the invention.
  • one or more of the group containing niobium, titanium and vanadium can be optionally added in the duplex stainless steel of the invention, the contents of niobium and titanium being limited up to 0,1 weight % and the vanadium content being limited to less than 0,2 weight %.
  • Boron, calcium and/or cerium can also be optionally added in small quantities in duplex stainless steels of the invention. The levels are for boron and calcium, less than 0,003 weight % and for cerium less than 0,1 weight %.
  • titanium (Ti), vanadium (V) and niobium (Nb) belong to a group of additions so named because they significantly change the steels properties at low concentrations, often beneficial effects in carbon steel but in the case of duplex stainless steels they also contribute to undesired property changes, such as reduced impact properties, higher surface defects levels and reduced ductility during casting and hot rolling and removal of nitrogen from solid solution. Many of these effects depend on their strong affinity for carbon and nitrogen, in particular nitrogen in the case of modern duplex stainless steels.
  • niobium and titanium should be limited to maximum level of 0,1% whereas vanadium is less detrimental and should be less than 0,2%.
  • the chemical compositions for the duplex stainless steels of the invention used in the following tests are given in the Table 1.
  • the Table 1 also contains the chemical compositions for the known duplex stainless steels LDX 2101®, LDX 2404®, 2304, 2205 and 2507 (alloys 22-26) used in the tests as the reference materials.
  • the duplex ferritic austenitic stainless steels according to the invention were tested by the Huey test for the corrosion resistance in nitric acid. This also provides an assessment of the susceptibility for intergranular corrosion and an indicative measure of the performance of the steel in urea production at elevated temperatures and pressures.
  • Huey test ASTM A262, practice C
  • the corrosion testing of the steel is made in a boiling solution of nitric acid so that the samples are boiled for 5 consecutive periods of 48 hours each in 65% nitric acid, each period starting with fresh acid.
  • the corrosion rate is calculated for each period from weight losses. The weight of metal lost is converted into loss in mm/year (millimeter per year).
  • the formula for the HRE value indicates that chromium and more so nickel have a large positive influence on the Huey test, while manganese is negative in this respect. Molybdenum and nitrogen are shown to have less effect. The effect of copper is so small as to be excluded from the equation.
  • the pitting resistance equivalent (PRE) for the duplex stainless steels of the Table 1 is calculated using the formula (2), the values of each element being in weight %:
  • PRE Cr + 3,3 ⁇ Mo + 30 ⁇ N ⁇ Mn Table 2 Steel Corrosion rate mm/y HRE PRE 1 0,135 42 39 2 0,115 37 43 3 0,114 39 44 4 0,122 39 39 5 0,090 40 42 6 0,119 42 39 7 0,122 41 42 22 (LDX 2101) 0,443 17 23 23 (2304) 0,222 27 26 24 (LDX 2404) 0,255 26 34 27 0,134 36 42 28 0,102 37 43 29 0,131 36 41 30 0,118 37 42 31 0,131 37 42 32 0,138 36 40 33 0,157 38 41 34 0,116 37 41
  • the corrosion rates presented in the Table 2 are illustrated in Figure 1 as a function of the HRE value.
  • the results presented in Figure 1 show the combined effect of the alloying elements as described above in the HRE and further show that the greater the Huey equivalent is, the smaller the corrosion rate.
  • the HRE value is advantageously limited to a minimum values of 35 which in the Huey test corresponds to a corrosion rate of 0,14 mm/year.
  • the pitting resistance equivalent value (PRE) in the duplex stainless steel of the invention is at the range of more than 41.
  • SRE sulphuric acid resistance equivalent
  • the sulphuric acid corrosion resistance SRE according to the formula (3) for the duplex stainless steel of the invention is above 8 at the boiling temperature (BT, 104 °C) of sulphuric acid, above 11 at the temperature 95°C and above 20 at the temperature 65°C.
  • the structural stability for the duplex ferritic austenitic stainless steel of the invention was tested by determining the sigma phase content. All the tested alloys were heat treated at the temperature of 850 °C for 10 min because of fastest kinetics in sigma phase formation at this temperature. After the heat treatment and cooling of the alloy the sigma phase content was metallographically determined.
  • the sigma equivalent shows a general formula for the structural stability for high alloyed duplex ferritic austenitic stainless steels.
  • the SGR value is advantageously limited to less than 18.
  • the results concerning the sigma phase content and the sigma equivalent (SGR) in the tested alloys are presented in the Table 4 and are illustrated in the Figure 3 showing the measured sigma phase content as a function of the sigma equivalent (SGR).
  • the selected alloys of the invention show a significantly lower tendency of SGR values for sigma phase formation than the alloy 25 (2507) which is well known for production difficulties and for sigma phase brittle behavior in processing lines.
  • duplex ferritic austenitic stainless steel according to the invention with a composition of 1,2%Mn, 2,1%Cu, 2,0%Mo and 0,3%N, is illustrated by the chemical composition window of Cr and Ni, i.e. the dependence between the contents of Cr and Ni in weight %, which lies within the frame of the area 5a', 5b', 5c', 5d' and 5e' in Figure 4 , and is defined with the following labelled positions of the coordinates in weight % in the Table 5.
  • the labelled positions in the Table 5 for the duplex stainless steel of the invention are determined with the desired values for ferrite content in the microstructure, PRE, SRE, HRE and SGR as shown in Figure 4 .
  • duplex ferritic austenitic stainless steel according to the invention with a composition of 1%Mn, 6,5% Ni, 1,8%Mo and 0,3%N, is illustrated by the chemical composition window of Cr and Cu in weight %, i.e. the dependence between the contents of Cr and Cu, which lies within the frame of the area 6a', 6b', 6c', 6d', 6e' and 6f' in Figure 5 , and is defined with the following labelled positions of the coordination in weight % in the Table 6.
  • the labelled positions in the Table 6 for the duplex stainless steel of the invention are determined with the desired values of ferrite content in the microstructure, PRE, SRE, SGR and the Cu content as shown in Figure 5 .
  • duplex ferritic austenitic stainless steel according to the invention with a composition of 1%Mn, 27,5% Cr, 1,8%Mo and 0,3%N, is illustrated by the chemical composition window of Ni and Cu, i.e. the dependence between the contents Ni and Cu in weight %, which lies within the frame of the area 7a', 7b', 7c', 7d' and 7e' in Figure 6 , is defined with the following labelled positions of the coordination in weight % in the Table 7.
  • the labelled positions in the Table 7 for the duplex stainless steel of the invention are determined with the desired values of ferrite content in the microstructure, SRE, SGR and the Cu content as shown in Figure 6 .
  • the sigma equivalent (SGR) according to the formula (4) in the alloys 27 - 34 is below 19.
  • This condition means that the formation of the sigma phase in the microstructure of the duplex stainless steel according to the invention is essentially prevented.
  • duplex stainless steels of the invention An important property of duplex stainless steels of the invention is the ease of the manufacture of these steels.
  • the hot workability and sensitivity to precipitation of intermetallic phases during hot working will be key elements to a successful high volume production of such grade.
  • the properties of the precipitated phases will not be the limiting factor during the actual hot working but during the following cold operations involving such simple tasks as lifting and transporting and more elaborate operations such as levelling of plates and uncoiling coils etc., a duplex steel with excessive amounts of sigma phase will be as brittle as glass and cannot be handled in a normal steel mill operation.
  • the hot workability issues have in the present invention been addressed by controlling the key minor elements such as boron (B), calcium (Ca) and cerium (Ce) sulphur (S) and aluminium (Al).
  • the sensibility to intermetallic phase precipitation is controlled by the major alloying elements Cr, Ni, Mo, Mn, Si, Cu and optionally W and Co as described in the section above regarding sigma equivalent in combination with hot rolling parameters.
  • duplex ferritic austenitic steel of the invention can be produced as castings, ingots, slabs, blooms, billets and flat products such as plates, sheets, strips, coils, and long products such as bars, rods, wires, profiles and shapes, seamless and welded tubes and/or pipes. Further, additional products such as metallic powder, formed shapes and profiles can be produced.

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Claims (11)

  1. Ferritisch-austenitischer rostfreier Duplexstahl zur Benutzung in der Chemieindustrie für Salpetersäureumgebungen, wobei gute einheitliche Korrosionsbeständigkeit und hohe Festigkeit erforderlich sind, dadurch gekennzeichnet, dass das Gefüge des rostfreien Stahl aus 35 bis 65 Volumen-% Ferrit besteht, der Rest Austenit ist und die chemische Zusammensetzung besteht aus weniger als 0,03 Gewichts-% Kohlenstoff, weniger als 1 Gewichts-% Silicium, 3 Gewichts-% oder weniger Mangan, 26 bis 29,5 Gewichts-% Chrom, 5 bis 8,5 Gewichts-% Nickel, 1 bis 3 Gewichts-% Molybdän, 0,25 bis 0,35 Gewichts-% Stickstoff, 1 bis 3 Gewichts-% Kupfer, wahlweise einem oder mehreren zugesetzten Elementen: weniger als 0,04 Gewichts-% AI, bevorzugt weniger als 0,03 Gewichts-% AI, weniger als 0,003 Gewichts-% B, weniger als 0,003 Gewichts-% Ca, weniger als 0,1 Gewichts-% Ce, bis zu 1 Gewichts-% Co, bis zu 1 Gewichts-% W, bis zu 0,1 Gewichts-% Nb, bis zu 0,1 Gewichts-% Ti, weniger als 0,2 Gewichts-% V, weniger als 0,010 Gewichts-% S, bevorzugt weniger als 0,005 Gewichts-% S, weniger als 0,040 Gewichts-% P, sodass die Summe aus S + P weniger als 0,04 Gewichts-% beträgt und der gesamte Sauerstoffgehalt unter 100 ppm, bevorzugt unter 50 ppm, beträgt, außer im Falle von Metallpulver, wobei der gesamte Sauerstoffgehalt bis zu 250 ppm beträgt, der Rest Eisen und unvermeidbare Verunreinigungen sind, die in rostfreien Stählen vorkommen, und dass das Sigmaäquivalent SGR, berechnet unter Benutzen der Formel Cr + 2 x Mo - 40 x N + 0,5 x Mn - 2 x Cu, weniger als 18 beträgt, das Huey-Äquivalent HRE, berechnet unter Benutzen der Formel Cr + 1,5 x Ni - 1,4 x Mn + 0,6 x Mo + 0,1 x N, in dem Bereich von 35 bis 39,5 ist und dass der Äquivalenzwert der Lochfraßbeständigkeit PRE, berechnet unter Benutzen der Formel Cr + 3,3 x Mo + 30 x N - Mn, in dem Bereich von mehr als 41 ist.
  2. Ferritisch-austenitischer rostfreier Duplexstahl nach Anspruch 1, dadurch gekennzeichnet, dass das Gefüge des rostfreien Stahls aus 45 bis 55 Volumen-% Ferrit besteht, wobei der Rest Austenit ist.
  3. Ferritisch-austenitischer rostfreier Duplexstahl nach einem der vorhergehenden Ansprüche, dadurch gekennzeichnet, dass die Korrosionsbeständigkeit gegen Schwefelsäure SRE, berechnet unter Benutzen der Formel Cr + 0,4 x Ni - 1,1 x Mn + 0,75 x Mo + 2,2 x Cu + 24 x N - 0,3 x T, wobei T die Prüftemperatur in °C ist, bei der Siedetemperatur von Schwefelsäure von 104 °C über 8, bei der Temperatur von 95 °C über 11 und bei der Temperatur von 65 °C über 20 beträgt.
  4. Ferritisch-austenitischer rostfreier Duplexstahl nach einem der vorhergehenden Ansprüche, dadurch gekennzeichnet, dass der Chromgehalt bevorzugt 26,5 bis 29 Gewichts-%, bevorzugter 27 bis 28,5 Gewichts-%, beträgt.
  5. Ferritisch-austenitischer rostfreier Duplexstahl nach einem der vorhergehenden Ansprüche, dadurch gekennzeichnet, dass der Nickelgehalt bevorzugt 5,5 bis 7,5 Gewichts-%, bevorzugter 5,8 bis 7,5 Gewichts-%, beträgt.
  6. Ferritisch-austenitischer rostfreier Duplexstahl nach einem der vorhergehenden Ansprüche, dadurch gekennzeichnet, dass der Mangangehalt bevorzugt 0,5 bis 1,5 Gewichts-% beträgt.
  7. Ferritisch-austenitischer rostfreier Duplexstahl nach einem der vorhergehenden Ansprüche, dadurch gekennzeichnet, dass der Kupfergehalt bevorzugt 1,3 bis 2,5 Gewichts-% beträgt.
  8. Ferritisch-austenitischer rostfreier Duplexstahl nach einem der vorhergehenden Ansprüche, dadurch gekennzeichnet, dass der Molybdängehalt bevorzugt 1,5 bis 2,5 Gewichts-% beträgt.
  9. Ferritisch-austenitischer rostfreier Duplexstahl nach einem der vorhergehenden Ansprüche, dadurch gekennzeichnet, dass der Stickstoffgehalt bevorzugt 0,25 bis 0,33 Gewichts-% beträgt.
  10. Ferritisch-austenitischer rostfreier Duplexstahl nach einem der vorhergehenden Ansprüche, dadurch gekennzeichnet, dass der Siliciumgehalt bevorzugt weniger als 0,6 Gewichts-% beträgt.
  11. Ferritisch-austenitischer rostfreier Duplexstahl nach einem der vorhergehenden Ansprüche, dadurch gekennzeichnet, dass der Stahl als Gusserzeugnisse, Barren, Brammen, Luppen, Knüppel, Platten, Bleche, Bänder, Bandringe, Stäbe, Stangen, Drähte, Profile und Gebilde, nahtlose und geschweißte Schläuche und/oder Rohre, Metallpulver, geformte Gebilde und Profile hergestellt ist.
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FI20110384A FI125854B (fi) 2011-11-04 2011-11-04 Dupleksi ruostumaton teräs
PCT/FI2012/051065 WO2013064746A1 (en) 2011-11-04 2012-11-01 Duplex stainless steel

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US20150050180A1 (en) 2015-02-19
US9637813B2 (en) 2017-05-02
TWI546391B (zh) 2016-08-21
CN103975088B (zh) 2016-08-24
FI20110384A (fi) 2013-05-05
EP2773785A1 (de) 2014-09-10
CN103975088A (zh) 2014-08-06
JP2014532811A (ja) 2014-12-08
IN2014MN00821A (de) 2015-07-03
JP5870201B2 (ja) 2016-02-24
TW201323629A (zh) 2013-06-16
WO2013064746A1 (en) 2013-05-10
EP2773785A4 (de) 2015-07-08
FI125854B (fi) 2016-03-15

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